High strength steel sheet having superior workability and method for manufacturing same

ABSTRACT

Provided is a steel sheet which can be used for automobile parts and the like, and relates to a steel sheet having a superior balance of strength and ductility and strength and hole expansion ratio and superior bending formability, and a method for manufacturing same.

TECHNICAL FIELD

The present invention relates to a steel sheet that may be used for automobile parts and the like, and to a steel sheet having high strength characteristics and superior workability and a method for manufacturing same.

BACKGROUND ART

In recent years, the automobile industry is paying attention to ways to reduce material weight and secure occupant stability in order to protect the global environment. In order to meet these requirements for stability and weight reduction, the application of a high strength steel sheet is rapidly increasing. In general, it has been known that as the strength of the steel sheet increases, the workability of the steel sheet decreases. Therefore, in the steel sheet for automobile parts, a steel sheet having superior workability represented by ductility, bendability, and hole expansion ratio while having high strength characteristics is required.

As a technique for improving workability of a steel sheet, a method of utilizing tempered martensite is disclosed in Patent Documents 1 and 2. Since the tempered martensite made by tempering hard martensite is softened martensite, there is a difference in strength between the tempered martensite and the existing untempered martensite (fresh martensite). Therefore, when fresh martensite is suppressed and the tempered martensite is formed, the workability may be increased.

However, by the techniques disclosed in Patent Documents 1 and 2, a balance (TSXE1) of tensile strength and elongation does not satisfy 22,000 MPa % or more, which means that it is difficult to secure a steel sheet having superior strength and ductility.

Meanwhile, transformation induced plasticity (TRIP) steel using transformation-induced plasticity of retained austenite was developed in order to obtain both high strength and superior workability for automobile member steel sheets. Patent Document 3 discloses TRIP steel having superior strength and workability.

Patent Document 3 discloses improving high ductility and workability by including polygonal ferrite, retained austenite, and martensite, but it can be seen that Patent Document 3 uses bainite as a main phase, and thus, the high strength is not secured and the balance (TSXE1) of tensile strength and elongation also does not satisfy 22,000 MPa % or more.

That is, the demand for a steel sheet having superior workability, such as ductility, bendability, and hole expansion ratio while having high strength, is not satisfied.

RELATED ART DOCUMENT

(Patent Document 1) Korean Patent Laid-Open Publication No. 10-2006-0118602

(Patent Document 2) Japanese Patent Laid-Open Publication No. 2009-019258

(Patent Document 3) Korean Patent Laid-Open Publication No. 10-2014-0012167

DISCLOSURE Technical Problem

The present invention provides a high strength steel sheet having superior ductility, bending formability, and hole expansion ratio by optimizing a composition and microstructure of the steel sheet and a method for manufacturing the same.

An object of the present invention is not limited to the abovementioned contents. Additional problems of the present invention are described in the overall content of the specification, and those of ordinary skill in the art to which the present invention pertains will have no difficulty in understanding the additional problems of the present invention from the contents described in the specification of the present invention.

Technical Solution

In an aspect of the present invention, a high strength steel sheet having superior workability may include: by wt %, C: 0.25 to 0.75%, Si: 4.0% or less, Mn: 0.9 to 5.0%, Al: 5.0% or less, P: 0.15% or less, S: 0.03% or less, N: 0.03% or less, a balance of Fe, and unavoidable impurities, and include, as microstructures, 30 to 70 vol % of tempered martensite, 10 to 45 vol % of bainite, 10 to 40 vol % of retained austenite, 3 to 20 vol % of ferrite, and unavoidable structures, and may satisfy the following [Relational Expression 1],

1.02≤[Si+Al]_(F)/[Si+Al]_(av)≤1.45  [Relational Expression 1]

where [Si+Al]_(F) is an average total content (wt %) of Si and Al included in the ferrite, and [Si+Al]_(av) is an average total content (wt %) of Si and Al included in the retained austenite.

The steel sheet may further include one or more of the following (1) to (9).

(1) one or more of Ti: 0 to 0.5%, Nb: 0 to 0.5%, and V: 0 to 0.5%;

(2) one or more of Cr: 0 to 3.0% and Mo: 0 to 3.0%;

(3) one or more of Cu: 0 to 4.5% and Ni: 0 to 4.5%;

(4) B: 0 to 0.005%;

(5) one or more of Ca: 0 to 0.05%, REM: 0 to 0.05% excluding Y, and Mg: 0 to 0.05%;

(6) one or more of W: 0 to 0.5% and Zr: 0 to 0.5%;

(7) one or more of Sb: 0 to 0.5% and Sn: 0 to 0.5%;

(8) one or more of Y: 0 to 0.2% and Hf: 0 to 0.2%; and

(9) Co: 0 to 1.5%

A total content (Si+Al) of Si and Al may be 1.0 to 6.0 wt %.

A balance B_(T·E) of tensile strength and elongation expressed by the following [Relational Expression 2] may be 22,000 (MPa %) or more, a balance B_(T·H) of tensile strength and hole expansion ratio expressed by the following [Relational Expression 3] may be 7*10⁶ (MPa²%^(1/2)) or more, and bendability B_(R) expressed by the following [Relational Expression 4] may be a range of 0.5 to 3.0.

B _(T·E)=[Tensile Strength(TS, MPa)]²*[Elongation(El, %)]   [Relational Expression 2]

B _(T·H)=[Tensile Strength(TS, MPa)]²*[Hole Expansion Ratio(HER, %)]^(1/2)  [Relational Expression 3]

B _(R) =R/t  [Relational Expression 4]

In the above Relational Expression 4, R is a minimum bending radius (mm) at which cracks do not occur after a 90° bending test, and t is a thickness (mm) of the steel sheet.

In another aspect of the present invention, a manufacturing method for high strength steel sheet having superior workability may include: heating and hot rolling a steel slab including, by wt %, C: 0.25 to 0.75%, Si: 4.0% or less, Mn: 0.9 to 5.0%, Al: 5.0% or less, P: 0.15% or less, S: 0.03% or less, N: 0.03% or less, a balance of Fe, and unavoidable impurities; coiling the hot-rolled steel sheet; performing hot-rolled annealing heat treatment on the coiled steel sheet in a temperature within a range of 650 to 850° C. for 600 to 1700 seconds; cold rolling the hot-rolled annealing heat-treated steel sheet; heating (primarily heating) the cold-rolled steel sheet to a temperature within a range of Ac1 or higher and less than Ac3 at an average temperature increase rate of 5° C./s or more, and maintaining (primarily maintaining) the primarily heated steel sheet for 50 seconds or more; cooling (primarily cooling) the primarily heated steel sheet to a temperature within a range of 100 to 300° C. at an average cooling rate of 1° C./s or more; heating (secondarily heating) the primarily cooled steel sheet to a temperature within a range of 300 to 500° C., and maintaining (secondarily maintaining) the primarily cooled steel sheet for 50 seconds or more; and cooling (secondarily cooling) the primarily cooled steel sheet to room temperature.

The steel slab may further include one or more of the following (1) to (9).

(1) one or more of Ti: 0 to 0.5%, Nb: 0 to 0.5%, and V: 0 to 0.5%;

(2) one or more of Cr: 0 to 3.0% and Mo: 0 to 3.0%;

(3) one or more of Cu: 0 to 4.5% and Ni: 0 to 4.5%;

(4) B: 0 to 0.005%;

(5) one or more of Ca: 0 to 0.05%, REM: 0 to 0.05% excluding Y, and Mg: 0 to 0.05%;

(6) one or more of W: 0 to 0.5% and Zr: 0 to 0.5%;

(7) one or more of Sb: 0 to 0.5% and Sn: 0 to 0.5%;

(8) one or more of Y: 0 to 0.2% and Hf: 0 to 0.2%; and

(9) Co: 0 to 1.5%.

A total content (Si+Al) of Si and Al included in the steel slab may be 1.0 to 6.0 wt %.

The steel slab may be heated to a temperature within a range of 1000 to 1350° C., and may be subjected to finish hot rolling in a temperature within a range of 800 to 1000° C.

The hot-rolled steel sheet may be coiled in a temperature within a range of 300 to 600° C.

A reduction ratio of the cold rolling may be 30 to 90%.

The cooling rate of the secondary cooling may be 1° C./s or more.

Advantageous Effects

According to an aspect of the present disclosure, it is possible to provide a steel sheet particularly suitable for automobile parts because the steel sheet has superior strength as well as superior workability such as ductility, bending formability, and hole expansion ratio.

BEST MODE

The present invention relates to a high strength steel sheet having superior workability and a method for manufacturing the same, and exemplary embodiments in the present invention will hereinafter be described. Exemplary embodiments in the present invention may be modified into several forms, and it is not to be interpreted that the scope of the present invention is limited to exemplary embodiments described below. The present exemplary embodiments are provided in order to further describe the present invention in detail to those skilled in the art to which the present invention pertains.

The inventors of the present invention recognized that, in a transformation induced plasticity (TRIP) steel including bainite, tempered martensite, retained austenite, and ferrite, when controlling a ratio of specific components included in the retained austenite and the ferrite to a certain range while promoting stabilization of the retained austenite, it is possible to simultaneously secure workability and strength of a steel sheet by reducing an inter-phase hardness difference of the retained austenite and the ferrite. Based on this, the present inventors have reached the present invention by devising a method capable of improving ductility and workability of the high strength steel sheet.

Hereinafter, a high strength steel sheet having superior workability according to an aspect of the present invention will be described in more detail.

In an aspect of the present invention, a high strength steel sheet having superior workability may include: by wt %, C: 0.25 to 0.75%, Si: 4.0% or less, Mn: 0.9 to 5.0%, Al: 5.0% or less, P: 0.15% or less, S: 0.03% or less, N: 0.03% or less, a balance of Fe, and unavoidable impurities, and include, as microstructures, 30 to 70 vol % of tempered martensite, 10 to 45 vol % of bainite, 10 to 40 vol % of retained austenite, 3 to 20 vol % of ferrite, and unavoidable structures, and may satisfy the following [Relational Expression 1].

1.02≤[Si+Al]_(F)/[Si+Al]_(av)≤1.45  [Relational Expression 1]

in the above Relational Expression 1, [Si+Al]_(F) is an average total content (wt %) of Si and Al included in the ferrite, and [Si+Al]_(av) is an average total content (wt %) of Si and Al included in the retained austenite.

Hereinafter, compositions of steel according to the present invention will be described in more detail. Hereinafter, unless otherwise indicated, % indicating a content of each element is based on weight.

The high strength steel sheet having superior workability according to an aspect of the present invention includes, by weight, C: 0.25 to 0.75%, Si: 4.0% or less, Mn: 0.9 to 5.0%, Al: 5.0% or less, P: 0.15% or less, S: 0.03% or less, N: 0.03% or less, a balance of Fe, and unavoidable impurities. In addition, the high strength steel sheet may further include one or more of Ti: 0.5% or less (including 0%), Nb: 0.5% or less (including 0%), V: 0.5% or less (including 0%), Cr: 3.0% or less (including 0%), Mo: 3.0% or less (including 0%), Cu: 4.5% or less (including 0%), Ni: 4.5% or less (including 0%), B: 0.005% or less (including 0%), Ca: 0.05% or less (including 0%), REM: 0.05% or less (including 0%) excluding Y, Mg: 0.05% or less (including 0%), W: 0.5% or less (including 0%), Zr: 0.5% or less (including 0%), Sb: 0.5% or less (including 0%), Sn: 0.5% or less (including 0%), Y: 0.2% or less (including 0%), Hf: 0.2% or less (including 0%), Co: 1.5% or less (including 0%). In addition, a total content (Si+Al) of Si and Al may be 1.0 to 6.0%.

Carbon (C): 0.25 to 0.75%

Carbon (C) is an unavoidable element for securing strength of a steel sheet, and is also an element for stabilizing the retained austenite that contributes to the improvement in ductility of the steel sheet. Accordingly, the present invention may include 0.25% or more of carbon (C) to achieve such an effect. A preferable content of carbon (C) may exceed 0.25%, may be 0.27% or more, and may be 0.30% or more. The more preferable content of carbon (C) may be 0.31% or more. On the other hand, when the content of carbon (C) exceeds a certain level, cold rolling may become difficult due to an excessive increase in strength. Therefore, an upper limit of the content of carbon (C) of the present disclosure may be limited to 0.75%. The content of carbon (C) may be 0.70% or less, and the more preferable content of carbon (C) may be 0.67% or less.

Silicon (Si): 4.0% or less (excluding 0%)

Silicon (Si) is an element that contributes to improvement in strength by solid solution strengthening, and is also an element that improves workability by strengthening ferrite and homogenizing a structure. In addition, silicon (Si) is an element contributing to a generation of the retained austenite by suppressing precipitation of cementite. Therefore, in the present invention, silicon (Si) may be necessarily added to achieve such an effect. The preferable content of silicon (Si) may be 0.02% or more, and the more preferable content of silicon (Si) may be 0.05% or more. However, when the content of silicon (Si) exceeds a certain level, a problem of plating defects, such as non-plating, may be induced during plating, and weldability of a steel sheet may be lowered, so the present invention may limit the upper limit of the silicon (Si) content to 4.0%. The preferable upper limit of the content of silicon (Si) may be 3.8%, and the more preferable upper limit of the content of silicon (Si) may be 3.5%.

Aluminum (Al): 5.0% or less (excluding 0%)

Aluminum (Al) is an element that performs deoxidation by combining with oxygen in steel. In addition, aluminum (Al) is also an element for stabilizing the retained austenite by suppressing precipitation of cementite like silicon (Si). Therefore, in the present invention, aluminum (Al) may be necessarily added to achieve such an effect. A preferable content of aluminum (Al) may be 0.05% or more, and a more preferable content of aluminum (Al) may be 0.1% or more. On the other hand, when aluminum (Al) is excessively added, inclusions in a steel sheet increase, and the workability of the steel sheet may be lowered, so the present invention may limit the upper limit of the content of aluminum (Al) to 5.0%. The preferable upper limit of the content of aluminum (Al) may be 4.75%, and the more preferable upper limit of the content of aluminum (Al) may be 4.5%.

Meanwhile, the total content (Si+Al) of silicon (Si) and aluminum (Al) is preferably 1.0 to 6.0%. Since silicon (Si) and aluminum (Al) are components that affect microstructure formation in the present invention, and thus, affect ductility, bending formability, and hole expansion ratio, the total content of silicon (Si) and aluminum (Al) is preferably 1.0 to 6.0%. The more preferable total content (Si+Al) of silicon (Si) and aluminum (Al) may be 1.5% or more, and may be 4.0% or less.

Manganese (Mn) 0.9 to 5.0%

Manganese (Mn) is a useful element for increasing both strength and ductility. Therefore, in the present disclosure, a lower limit of a content of manganese (Mn) may be limited to 0.9% in order to achieve such an effect. A preferable lower limit of the content of manganese (Mn) may be 1.0%, and a more preferable lower limit of the content of manganese (Mn) may be 1.1%. On the other hand, when manganese (Mn) is excessively added, the bainite transformation time increases and a concentration of carbon (C) in the austenite becomes insufficient, so there is a problem in that the desired austenite fraction may not be secured. Therefore, an upper limit of the content of manganese (Mn) of the present disclosure may be limited to 5.0%. A preferable upper limit of the content of manganese (Mn) may be 4.7%, and a more preferable upper limit of the content of manganese (Mn) may be 4.5%.

Phosphorus (P): 0.15% or less (including 0%)

Phosphorus (P) is an element that is included as an impurity and deteriorates impact toughness. Therefore, it is preferable to manage the content of phosphorus (P) to 0.15% or less.

Sulfur (S): 0.03% or less (including 0%)

Sulfur (S) is an element that is included as an impurity to form MnS in a steel sheet and deteriorate ductility. Therefore, the content of sulfur (S) is preferably 0.03% or less.

Nitrogen (N): 0.03% or less (including 0%)

Nitrogen (N) is an element that is contained as an impurity and forms nitride during continuous casting to causes cracks of slab. Therefore, the content of nitrogen (N) is preferably 0.03% or less.

Meanwhile, the steel sheet of the present invention has an alloy composition that may be additionally included in addition to the above-described alloy components, which will be described in detail below.

One or more of titanium (Ti): 0 to 0.5%, niobium (Nb): 0 to 0.5%, and vanadium (V): 0 to 0.5%

Titanium (Ti), niobium (Nb), and vanadium (V) are elements that make precipitates and refine crystal grains, and are elements that also contribute to the improvement in strength and impact toughness of a steel sheet, and therefore, in the present invention, one or more of titanium (Ti), niobium (Nb), and vanadium (V) may be added to achieve such an effect. However, when the content of titanium (Ti), niobium (Nb), and vanadium (V) exceed a certain level, respectively, excessive precipitates are formed to lower impact toughness and increase manufacturing cost, so the present invention may limit the content of titanium (Ti), niobium (Nb), and vanadium (V) to 0.5% or less, respectively.

One or more of chromium (Cr): 0 to 3.0% and molybdenum (Mo): 0 to 3.0%

Since chromium (Cr) and molybdenum (Mo) are elements that not only suppress austenite decomposition during alloying treatment, but also stabilize austenite like manganese (Mn), the present invention may add one or more of chromium (Cr) and molybdenum (Mo) to achieve such an effect. However, when the content of chromium (Cr) and molybdenum (Mo) exceeds a certain level, the bainite transformation time increases and the concentration of carbon (C) in austenite becomes insufficient, so the desired retained austenite fraction may not be secured. Therefore, the present invention may limit the content of chromium (Cr) and molybdenum (Mo) to 3.0% or less, respectively.

One or more of Cu: 0 to 4.5% and Ni: 0 to 4.5%

Copper (Cu) and nickel (Ni) are elements that stabilize austenite and suppress corrosion. In addition, copper (Cu) and nickel (Ni) are also elements that are concentrated on a surface of a steel sheet to prevent hydrogen from intruding into the steel sheet, to thereby suppress hydrogen delayed destruction. Accordingly, in the present invention, one or more of copper (Cu) and nickel (Ni) may be added to achieve such an effect. However, when the content of copper (Cu) and nickel (Ni) exceeds a certain level, not only excessive characteristic effects, but also an increase in manufacturing cost is induced, so the present invention may limit the content of copper (Cu) and nickel (Ni) to 4.5% or less, respectively.

Boron (B): 0 to 0.005%

Boron (B) is an element that improves hardenability to increase strength, and is also an element that suppresses nucleation of grain boundaries. Therefore, in the present invention, boron (B) may be added to achieve such an effect. However, when the content of boron (B) exceeds a certain level, not only excessive characteristic effects, but also an increases in manufacturing cost is induced, so the present invention may limit the content of boron (B) to 0.005% or less.

One or more of calcium (Ca): 0 to 0.05%, Magnesium (Mg): 0 to 0.05%, and rare earth element (REM) excluding yttrium (Y): 0 to 0.05%

Here, the rare earth element (REM) is scandium (Sc), yttrium (Y), and a lanthanide element. Since calcium (Ca), magnesium (Mg), and the rare earth element (REM) excluding yttrium (Y) are elements that contribute to the improvement in ductility of a steel sheet by spheroidizing sulfides, in the present invention, one or more of calcium (Ca), magnesium (Mg), and the rare earth element (REM) excluding yttrium (Y) may be added to achieve such an effect. However, when the content of calcium (Ca), magnesium (Mg), and the rare earth element (REM) excluding yttrium (Y) exceeds a certain level, not only excessive characteristic effects, but also an increase in manufacturing cost are induced, so the present invention may limit the content of calcium (Ca), magnesium (Mg), and the rare earth element (REM) excluding yttrium (Y) to 0.05% or less, respectively.

One or more of tungsten (W): 0 to 0.5% and zirconium (Zr): 0 to 0.5%

Since tungsten (W) and zirconium (Zr) are elements that increase strength of a steel sheet by improving hardenability, in the present invention, one or more of tungsten (W) and zirconium (Zr) may be added to achieve such an effect. However, when the content of tungsten (W) and zirconium (Zr) exceeds a certain level, not only excessive characteristic effects, but also an increase in manufacturing cost are induced, so the present invention may limit the content of tungsten (W) and zirconium (Zr) to 0.5% or less, respectively.

One or more of antimony (Sb): 0 to 0.5% and tin (Sn): 0 to 0.5%

Since antimony (Sb) and tin (Sn) are elements that improve plating wettability and plating adhesion of a steel sheet, in the present invention, one or more of antimony (Sb) and tin (Sn) may be added to achieve such an effect. However, when the content of antimony (Sb) and tin (Sn) exceeds a certain level, brittleness of a steel sheet increases, and thus, cracks may occur during hot working or cold working, so the present invention may limit the content of antimony (Sb) and tin (Sn) to 0.5% or less, respectively.

One or more of yttrium (Y): 0 to 0.2% and hafnium (Hf): 0 to 0.2%

Since yttrium (Y) and hafnium (Hf) are elements that improve corrosion resistance of a steel sheet, in the present invention, one or more of the yttrium (Y) and hafnium (Hf) may be added to achieve such an effect. However, when the content of yttrium (Y) and hafnium (Hf) exceeds a certain level, the ductility of the steel sheet may deteriorate, so the present invention may limit the content of yttrium (Y) and hafnium (Hf) to 0.2% or less, respectively.

Cobalt (Co): 0 to 1.5%

Since cobalt (Co) is an element that promotes bainite transformation to increase a TRIP effect, in the present invention, cobalt (Co) may be added to achieve such an effect. However, when the content of cobalt (Co) exceeds a certain level, since weldability and ductility of a steel sheet may deteriorate, the present invention may limit the content of cobalt (Co) to 1.5% or less.

The high strength steel sheet having superior workability according to an aspect of the present disclosure may include a balance of Fe and other unavoidable impurities in addition to the components described above. However, in a general manufacturing process, unintended impurities may inevitably be mixed from a raw material or the surrounding environment, and thus, these impurities may not be completely excluded. Since these impurities are known to those skilled in the art, all the contents are not specifically mentioned in the present specification. In addition, additional addition of effective components other than the above-described components is not entirely excluded.

The high strength steel sheet having superior workability according to an aspect of the present invention may include, as microstructures, tempered martensite, bainite, retained austenite, and ferrite. As a preferred example, the high strength steel sheet having superior workability according to an aspect of the present invention may include, by volume fraction, 30 to 70% of tempered martensite, 10 to 45% of bainite, 10 to 40% of retained austenite, 3 to 20% of ferrite, and an unavoidable structure. As the unavoidable structure of the present invention, fresh martensite, perlite, martensite austenite constituent (M-A), and the like may be included. When the fresh martensite or the pearlite is excessively formed, the workability of the steel sheet may be lowered or the fraction of the retained austenite may be lowered.

In the high-strength steel sheet having superior workability according to an aspect of the present invention, as shown in the following [Relational Expression 1], the ratio of the average total content ([Si+Al]_(F), wt %) of silicon (Si) and aluminum (Al) included in the ferrite to the average total content ([Si+Al]_(av), wt %) of silicon (Si) and aluminum (Al) included in the steel sheet may satisfy the range of 1.02 to 1.45.

1.02≤[Si+Al]_(F)/[Si+Al]_(av)≤1.45  [Relational Expression 1]

In addition, in the high strength steel sheet having superior workability according to an aspect of the present invention, since a balance B_(T·E) of tensile strength and elongation expressed by the following [Relational Expression 2] is 22,000 (MPa %) or more, a balance B_(T·H) of tensile strength and hole expansion ratio expressed by the following [Relational Expression 3] is 7*10⁶ (MPa²%^(1/2)) or more, and bendability B_(R) expressed by the following [Relational Expression 4] satisfies a range of 0.5 to 3.0, it may have a superior balance of strength and ductility, a balance of strength and hole expansion ratio, and superior bending formability.

B _(T·E)=[Tensile Strength(TS, MPa)]²*[Elongation(El, %)]   [Relational Expression 2]

B _(T·H)=[Tensile Strength(TS, MPa)]²*[Hole Expansion Ratio(HER, %)]^(1/2)  [Relational Expression 3]

B _(R) =R/t  [Relational Expression 4]

In the above Relational Expression 4, R is a minimum bending radius (mm) at which cracks do not occur after a 90° bending test, and t is a thickness (mm) of the steel sheet.

In the present invention, it is important to stabilize retained austenite of a steel sheet because it is intended to simultaneously secure superb ductility and bending formability as well as high strength properties. In order to stabilize the retained austenite, it is necessary to concentrate carbon (C) and manganese (Mn) in the ferrite, bainite, and tempered martensite of the steel sheet into austenite. However, when carbon (C) is concentrated into austenite by using ferrite, the strength of the steel sheet may be insufficient due to the low strength characteristics of ferrite, and excessive inter-phase hardness difference may occur, thereby reducing the hole expansion ratio (HER). Therefore, the present invention is intended to concentrate carbon (C) and manganese (Mn) into austenite by using the bainite and tempered martensite.

When the content of silicon (Si) and aluminum (Al) in the retained austenite is limited to a certain range, carbon (C) and manganese (Mn) may be concentrated in large amounts from bainite and tempered martensite into retained austenite, thereby effectively stabilizing the retained austenite. In addition, by limiting the content of silicon (Si) and aluminum (Al) in austenite to a certain range, it is possible to increase the content of silicon (Si) and aluminum (Al) in ferrite. As the content of silicon (Si) and aluminum (Al) in the ferrite increases, the hardness of the ferrite increases, so it is possible to effectively reduce an inter-phase hardness difference of ferrite which is a soft structure and tempered martensite, bainite, and retained austenite which are a hard structure.

Therefore, the present invention limits a ratio of an average total content ([Si+Al]_(F), wt %) of silicon (Si) and aluminum (Al) included in the ferrite to an average total content ([Si+Al]_(av), wt %) of silicon (Si) and aluminum (Al) included in the steel sheet to 1.02 or more, so the inter-phase hardness difference of the soft structure and the hard structure may be effectively reduced. On the other hand, when the content of silicon (Si) and aluminum (Al) in the ferrite is excessive, rather the ferrite is excessively hardened, and thus, the workability deteriorates, so the desired balance (TSXE1) of tensile strength and elongation, the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio, and the bendability (R/t) may not all be secured. Therefore, the present invention may limit the ratio of the average total content ([Si+Al]_(F), wt %) of silicon (Si) and aluminum (Al) included in the ferrite to the average total content ([Si+Al]_(av), wt %) of silicon (Si) and aluminum (Al) included in the steel sheet to 1.45 or more.

A steel sheet including retained austenite has superb ductility and bending formability due to transformation-induced plasticity that occurs during transformation from austenite to martensite during processing. When the fraction of the retained austenite is less than a certain level, the balance (TSXE1) of tensile strength and elongation may be less than 22,000 MPa %, or the bendability (R/t) may exceed 3.0. Meanwhile, when the fraction of the retained austenite exceeds a certain level, local elongation may be lowered. Accordingly, in the present invention, the fraction of the retained austenite may be limited to a range of 10 to 40 vol % in order to obtain a steel sheet having a balance (TSXE1) of tensile strength and elongation and superior bendability (R/t).

Meanwhile, both untempered martensite (fresh martensite) and tempered martensite are microstructures that improve the strength of the steel sheet. However, compared with the tempered martensite, fresh martensite has a characteristic of greatly reducing the ductility and the hole expansion ratio of the steel sheet. This is because the microstructure of the tempered martensite is softened by the tempering heat treatment. Therefore, in the present invention, it is preferable to use tempered martensite to provide a steel sheet which is superior in the balance of strength and ductility, the balance of strength and hole expansion ratio, and the bending formability. When the fraction of the tempered martensite is less than a certain level, it is difficult to secure the balance (TSXE1) of tensile strength and elongation of 22,000 MPa % or more or the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio of 7*10⁶ (MPa²%^(1/2)) or more, and when the fraction of the tempered martensite exceeds a certain level, ductility and workability is lowered, and the balance (TSXE1) of tensile strength and elongation is less than 22,000 MPa %, or bendability (R/t) exceeds 3.0, which is not preferable. Therefore, in the present invention, the fraction of the tempered martensite may be limited to 30 to 70 vol % to obtain a steel sheet having the balance (TSXE1) of tensile strength and elongation, the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio, and superb bendability (R/t).

In order to improve the balance (TSXE1) of tensile strength and elongation, the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio, and the bendability (R/t), it is preferable that bainite is appropriately included as the microstructure. As long as a fraction of bainite is a certain level or more, it is possible to secure the balance (TSXE1) of tensile strength and elongation of 22,000 MPa % or more, the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio of 7*10⁶ (MPa²%^(1/2)) or more and the bendability (R/t) of 0.5 to 3.0. On the other hand, when the fraction of bainite is excessive, the decrease in the fraction of tempered martensite is necessarily accompanied, so the present invention may not secure the desired balance (TSXE1) of tensile strength and elongation, the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio, and bendability (R/t). Accordingly, the present invention may limit the fraction of bainite to a range of 10 to 45 vol %.

Since ferrite is an element contributing to improvement in ductility, the present invention may secure the desired balance (TSXE1) of tensile strength and elongation, as long as the fraction of ferrite is a certain level or more. However, when the fraction of ferrite is excessive, the inter-phase hardness difference increases and the hole expansion ratio (HER) may decrease, so the present invention may not secure the desired balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio. Accordingly, the present invention may limit the fraction of ferrite to a range of 3 to 20 vol %.

Hereinafter, an example of a method for manufacturing a steel sheet of the present invention will be described in detail.

A method for manufacturing a high-strength steel sheet according to an aspect of the present invention may include: preparing a steel slab having a predetermined component, and heating and hot rolling the steel slab; coiling the hot-rolled steel sheet; performing hot-rolled annealing heat treatment on the coiled steel sheet in a temperature within a range of 650 to 850° C. for 600 to 1700 seconds; cold rolling the hot-rolled annealing heat-treated steel sheet; heating (primarily heating) the hot-rolled annealing heat-treated steel sheet to a temperature within a range of Ac1 or higher and less than Ac3 at an average temperature increase rate of 5° C./s or more, and maintaining (primarily maintaining) the primarily heated steel sheet for 50 seconds or more; cooling (primarily cooling) the primarily heated steel sheet to a temperature within a range of 100 to 300° C. at an average cooling rate of 1° C./s or more; heating (secondarily heating) the primarily cooled steel sheet to a temperature within a range of 300 to 500° C., and maintaining (secondarily maintaining) the primarily cooled steel sheet for 50 seconds or more; and cooling (secondarily cooling) the primarily cooled steel sheet to room temperature.

Preparation and Heating of Steel Slab

A steel slab having a predetermined component is prepared. Since the steel slab according to the present invention includes an alloy composition corresponding to an alloy composition of the steel sheet described above, the description of the alloy compositions of the slab is replaced by the description of the alloy composition of the steel sheet described above.

The prepared steel slab may be heated to a certain temperature range, and the heating temperature of the steel slab at this time may be in the range of 1000 to 1350° C. This is because, when the heating temperature of the steel slab is less than 1000° C., the steel slab may be hot rolled in the temperature range below the desired finish hot rolling temperature range, and when the heating temperature of the steel slab exceeds 1350° C., the temperature reaches a melting point of steel, and thus, the steel slab is melted.

Hot Rolling and Coiling

The heated steel slab may be hot rolled, and thus, provided as a hot-rolled steel sheet. During the hot rolling, the finish hot rolling temperature is preferably in the range of 800 to 1000° C. When the finish hot rolling temperature is less than 800° C., an excessive rolling load may be a problem, and when the finish hot rolling temperature exceeds 1000° C., grains of the hot-rolled steel sheet are coarsely formed, which may cause a deterioration in physical properties of the final steel sheet.

The hot-rolled steel sheet after the hot rolling has been completed may be cooled at an average cooling rate of 10° C./s or more, and may be coiled at a temperature of 300 to 600° C. When the coiling temperature is less than 300° C., the coiling is not easy, and when the coiling temperature exceeds 600° C., a surface scale is formed to the inside of the hot-rolled steel sheet, which may make pickling difficult.

Hot-Rolled Annealing Heat Treatment

It is preferable to perform a hot-rolled annealing heat treatment process in order to facilitate pickling and cold rolling, which are subsequent processes after the coiling. The hot-rolled annealing heat treatment may be performed in a temperature within a range of 650 to 850° C. for 600 to 1700 seconds. When the hot-rolled annealing heat treatment temperature is less than 650° C. or the hot-rolled annealing heat treatment time is less than 600 seconds, the strength of the hot-rolled annealing heat-treated steel sheet increases, and thus, subsequent cold rolling may not be easy. On the other hand, when the hot-rolled annealing heat treatment temperature exceeds 850° C. or the hot-rolled annealing heat treatment time exceeds 1700 seconds, the pickling may not be easy due to a scale formed deep inside the steel sheet.

Pickling and Cold Rolling

After the hot-rolled annealing heat treatment, in order to remove the scale generated on the surface of the steel sheet, the pickling may be performed, and the cold rolling may be performed. Although the conditions of the pickling and cold rolling are not particularly limited in the present invention, the cold rolling is preferably performed at a cumulative reduction ratio of 30 to 90%. When the cumulative reduction ratio of the cold rolling exceeds 90%, it may be difficult to perform the cold rolling in a short time due to the high strength of the steel sheet.

The cold-rolled steel sheet may be manufactured as a non-plated cold-rolled steel sheet through the annealing heat treatment process, or may be manufactured as a plated steel sheet through a plating process to impart corrosion resistance. As the plating, plating methods such as hot-dip galvanizing, electro-galvanizing, and hot-dip aluminum plating may be applied, and the method and type are not particularly limited.

Annealing Heat Treatment

In the present invention, in order to simultaneously secure the strength and workability of the steel sheet, the annealing heat treatment process is performed.

The cold-rolled steel sheet is heated (primarily heated) to a temperature within a range of Ac1 or higher and less than Ac3 (two-phase region), and maintained (primarily maintained) in the temperature range for 50 seconds or more. The primary heating or primary maintaining temperature is Ac3 or higher (single-phase region), the desired ferrite structure may not be realized, so the desired level of [Si+Al]_(F)/[Si+Al]_(av), and the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio may be implemented. In addition, when the primary heating or primary maintaining temperature is in a temperature range less than Ac1, there is a fear that sufficient heating is not made, and thus, the microstructure desired by the present invention may not be implemented even by subsequent heat treatment. The average temperature increase rate of the primary heating may be 5° C./s or more.

When the primary maintaining time is less than 50 seconds, the structure may not be sufficiently homogenized and the physical properties of the steel sheet may be lowered. The upper limit of the primary maintaining time is not particularly limited, but the primary heating time is preferably limited to 1200 seconds or less in order to prevent the decrease in toughness due to the coarsening of grains.

After the primary maintaining, the cold-rolled steel sheet may be cooled (primarily cooled) to a primary cooling stop temperature of 100 to 300° C. at a primary cooling rate of an average cooling rate of 1° C./s or more. The upper limit of the primary cooling rate does not need to be particularly specified, but is preferably limited to 100° C./s or less. When the primary cooling stop temperature is less than 100° C., the tempered martensite is excessively formed and the amount of retained austenite formed is insufficient, so [Si+Al]_(F)/[Si+Al]_(av), the balance (TSXE1) of tensile strength and elongation, and the bendability (R/t) may be lowered. On the other hand, when the primary cooling stop temperature exceeds 300° C., the bainite is excessively formed and the amount of tempered martensite formed is insufficient, so the balance (TSXE1) of tensile strength and elongation of the steel sheet, and the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio of the steel sheet may be lowered.

After the primary cooling, the cold-rolled steel sheet may be heated (secondarily heated) to a secondary heating temperature of 300 to 500° C. at a secondary heating rate of an average temperature increase rate of 5° C./s or more, and may be maintained (secondarily maintained) for 50 seconds or more in the temperature range. The upper limit of the secondary temperature increase rate does not need to be particularly specified, but is preferably limited to 100° C./s or less. When the secondary heating or secondary maintaining temperature is less than 300° C., or the maintaining time is less than 50 seconds, the tempered martensite is excessively formed and the control of Si and Al content in the steel sheet is insufficient, so the desired fraction of the retained austenite is difficult to secure. As a result, [Si+Al]_(F)/[Si+Al]_(av), the balance (TSXE1) of tensile strength and elongation and the bendability (R/t) may be lowered. On the other hand, when the secondary heating or maintaining temperature exceeds 500° C. or the secondary maintaining time exceeds 126,000 seconds, it is difficult to secure the fraction of the retained austenite because the control of Si and Al content in the steel sheet is insufficient. As a result, [Si+Al]_(F)/[Si+Al]_(av), and the balance (TSXE1) of tensile strength and elongation may be lowered.

After the secondary maintaining, it is preferable to cool (secondarily cool) the cold-rolled steel sheet to room temperature at an average cooling rate of 1° C./s or more.

The high strength steel sheet having superior workability manufactured by the above-described manufacturing method may include, as a microstructure, tempered martensite, bainite, retained austenite, and ferrite, and as a preferred example, may include, by the volume fraction, 30 to 70% of tempered martensite, 10 to 45% of bainite, 10 to 40% of retained austenite, 3 to 20% of ferrite, and unavoidable structures.

In addition, in the high-strength steel sheet having superior workability manufactured by the above-described manufacturing method, as in the following [Relational Expression 1], the ratio of the average total content ([Si+Al]_(F), wt %) of silicon (Si) and aluminum (Al) included in the ferrite to the average total content ([Si+Al]_(av), wt %) of silicon (Si) and aluminum (Al) included in the steel sheet may satisfy a range of 1.02 to 1.45, and the balance B_(T·E) of tensile strength and elongation expressed by the following [Relational Expression 2] is 22,000 (MPa %) or more, the balance B_(T·H) of tensile strength and hole expansion ratio expressed by the following [Relational Expression 3] may be 7*10⁶ (MPa²%^(1/2)) or more, and the bendability B_(R) expressed by the following [Relational Expression 4] may satisfy the range of 0.5 to 3.0.

1.02≤[Si+Al]_(F)/[Si+Al]_(av)≤1.45  [Relational Expression 1]

B _(T·E)=[Tensile Strength(TS, MPa)]²*[Elongation(El, %)]   [Relational Expression 2]

B _(T·H)=[Tensile Strength(TS, MPa)]²*[Hole Expansion Ratio(HER, %)]^(1/2)  [Relational Expression 3]

B _(R) =R/t  [Relational Expression 4]

In the above Relational Expression 4, R is a minimum bending radius (mm) at which cracks do not occur after a 90° bending test, and t is a thickness (mm) of the steel sheet.

MODE FOR INVENTION

Hereinafter, a high strength steel sheet having superior workability and a method for manufacturing same according to an aspect of the present invention will be described in more detail. It should be noted that the following examples are only for the understanding of the present invention, and are not intended to specify the scope of the present invention. The scope of the present invention is determined by matters described in claims and matters reasonably inferred therefrom.

Inventive Example

A steel slab having a thickness of 100 mm having alloy compositions (a balance of Fe and unavoidable impurities) shown in Table 1 below was prepared, heated at 1200° C., and then was subjected to finish hot rolling at 900° C. Thereafter, the steel slab was cooled at an average cooling rate of 30° C./s, and coiled at a coiling temperature of Tables 2 and 3 to manufacture a hot-rolled steel sheet having a thickness of 3 mm. The hot-rolled steel sheet was subjected to hot-rolled annealing heat treatment under the conditions of Tables 2 and 3. Thereafter, after removing a surface scale by pickling, cold rolling was performed to a thickness of 1.5 mm.

Thereafter, the heat treatment was performed under the annealing heat treatment conditions disclosed in Tables 2 to 5 to manufacture the steel sheet.

The microstructure of the thus prepared steel sheet was observed, and the results were shown in Tables 6 and 7. Among the microstructures, ferrite (F), bainite (B), tempered martensite (TM), and pearlite (P) were observed through SEM after nital-etching a polished specimen cross section. The fractions of bainite and tempered martensite, which are difficult to distinguish among them, were calculated using an expansion curve after evaluation of dilatation. Meanwhile, since fresh martensite (FM) and retained austenite (retained γ) are also difficult to distinguish, a value obtained by subtracting the fraction of retained austenite calculated by X-ray diffraction method from the fraction of martensite and retained austenite observed by the SEM was determined as the fraction of the fresh martensite.

Meanwhile, [Si+Al]_(F)/[Si+Al]_(av), a balance (TSXE1) of tensile strength and elongation, a balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio, and bendability (R/t) of the steel sheet were observed, and the results were shown in Tables 8 and 9.

An average total content ([Si+Al]_(F), wt %) of silicon (Si) and aluminum (Al) contained in ferrite was measured using an electron probe MicroAnalyser (EPMA), and an average total content ([Si+Al]_(av), wt %) of silicon (Si) and aluminum (Al) included in the steel sheet was calculated from the content of alloy composition of the steel sheet.

Tensile strength (TS) and elongation (El) were evaluated through a tensile test, and the tensile strength (TS) and the elongation (El) were measured by evaluating the specimens collected in accordance with JIS No. 5 standard based on a 90° direction with respect to a rolling direction of a rolled sheet. The bendability (R/t) was evaluated by a V-bending test, and calculated by collecting a specimen based on the 90° direction with respect to the rolling direction of the rolled sheet and being determined as a value obtained by dividing a minimum bending radius R, at which cracks do not occur after a 90° bending test, by a thickness t of a sheet. The hole expansion ratio (HER) was evaluated through the hole expansion test, and was calculated by the following [Relational Expression 5] by, after forming a punching hole (die inner diameter of 10.3 mm, clearance of 12.5%) of 10 mmØ, inserting a conical punch having an apex angle of 60° into a punching hole in a direction in which a burr of a punching hole faces outward, and then compressing and expanding a peripheral portion of the punching hole at a moving speed of 20 mm/min.

Hole expansion ratio (HER, %)={(D−D ₀)/D ₀}×100  [Relational Expression 5]

In the above Relational Expression 5, D is a hole diameter (mm) when cracks penetrate through the steel plate along the thickness direction, and D₀ is the initial hole diameter (mm).

TABLE 1 Steel Chemical Component (wt %) type C Si Mn P S Al N Cr Mo

A 0.36 1.77 1.79 0.009 0.0011 0.48 0.0028 0.64 B 0.34 2.15 1.65 0.011 0.0010 0.51 0.0034 0.31 0.28 C 0.37 1.86 1.96 0.010 0.0008 0.59 0.0025 0.53 D 0.35 1.58 3.87 0.008 0.0011 0.52 0.0033 0.45 E 0.38 1.73 2.25 0.010 0.0010 0.76 0.0034 F 0.43 1.59 2.16 0.012 0.0011 0.64 0.0028 G 0.70 1.62 1.84 0.008 0.0008 0.60 0.0031 H 0.33 1.14 2.03 0.011 0.0010 1.25 0.0030 I 0.37 0.65 1.93 0.008 0.0013 2.47 0.0024 J 0.39 0.03 2.25 0.010 0.0010 4.68 0.0033 Ti 0.04 K 0.46 1.57 2.57 0.008 0.0011 0.54 0.0034 Nb 0.05 L 0.49 1.94 1.94 0.009 0.0008 0.39 0.0021 V 0.04 M 0.34 1.83 2.02 0.010 0.0011 0.28 0.0030 Ni 0.38 N 0.35 1.59 2.36 0.011 0.0013 0.42 0.0033 Cu 0.32 O 0.36 1.55 1.64 0.013 0.0007 0.48 0.0027 B 0.003 P 0.43 1.62 2.11 0.012 0.0008 0.67 0.0022 Ca 0.001 Q 0.39 1.74 2.25 0.008 0.0009 0.59 0.0032 REM 0.001 R 0.42 1.69 2.03 0.008 0.0008 0.62 0.0030 Mg 0.002 S 0.35 1.75 2.14 0.009 0.0011 0.53 0.0037 W 0.12 T 0.32 2.04 2.20 0.011 0.0011 0.43 0.0041 Zr 0.10 U 0.34 1.62 2.17 0.009 0.0010 0.58 0.0035 Sb 0.02 V 0.38 1.80 2.12 0.008 0.0011 0.72 0.0042 Sn 0.01 W 0.37 1.54 2.04 0.010 0.0011 0.63 0.0028 Y 0.01 X 0.28 3.26 2.36 0.009 0.0007 0.49 0.0032 Hf 0.01 Y 0.34 2.18 2.25 0.011 0.0001 0.45 0.0027 Co 0.37 XA 0.22 1.79 2.14 0.008 0.0008 0.51 0.0023 XB 0.79 1.84 1.88 0.012 0.0008 0.53 0.0031 XC 0.36 0.02 1.96 0.008 0.0010 0.03 0.0035 XD 0.33 4.19 1.85 0.010 0.0011 0.03 0.0030 XE 0.37 0.02 2.02 0.012 0.0008 5.18 0.0023 XF 0.39 1.93 0.74 0.009 0.0011 0.47 0.0022 XG 0.41 1.77 5.32 0.011 0.0009 0.53 0.0030 XH 0.37 1.85 1.83 0.008 0.0011 0.58 0.0034 3.46 XI 0.42 1.82 2.17 0.010 0.0009 0.65 0.0023 3.52

TABLE 2 Coiling Annealing temperature temperature Annealing Primary Primary of hot- of hot- time of hot- average maintaining Primary Specimen Steel rolled steel rolled steel rolled steel heating temperature maintaining No. type sheet (° C.) sheet (° C.) sheet (s) rate (° C./s) section (° C.) time (s) 1 A 500 800 1400 10 Two- 120 phase region 2 A 550 900 1200 Poor pickling 3 A 550 600 1300 Occurrence of fracture during cold rolling 4 B 400 750 1800 Poor pickling 5 B 450 750 500 Occurrence of fracture during cold rolling 6 B 450 700 1200 10 Single- 120 phase Region 7 B 400 750 1600 10 Two- 120 phase region 8 B 500 800 1500 10 Two- 120 phase region 9 B 400 750 1000 10 Two- 120 phase region 10 B 550 750 1200 10 Two- 120 phase region 11 C 500 700 900 10 Two- 120 phase region 12 C 550 700 1200 10 Two- 120 phase region 13 C 450 750 1000 10 Two- 120 phase region 14 C 500 700 1400 10 Two- 120 phase region 15 C 500 750 1400 10 Two- 120 phase region 16 C 450 650 1300 10 Two- 120 phase region 17 C 550 650 1500 10 Two- 120 phase region 18 D 500 750 1200 10 Two- 120 phase region 19 E 500 650 1700 10 Two- 120 phase region 20 F 450 700 600 10 Two- 120 phase region 21 G 500 750 1300 10 Two- 120 phase region 22 H 450 850 800 10 Two- 120 phase region 23 I 350 700 1200 10 Two- 120 phase region 24 J 550 700 1300 10 Two- 120 phase region 25 K 500 800 1500 10 Two- 120 phase region

TABLE 3 Coiling Annealing temperature temperature Annealing Primary Primary of hot- of hot- time of hot- average maintaining Primary Specimen Steel rolled steel rolled steel rolled steel heating temperature maintaining No. type sheet (° C.) sheet (° C.) sheet (s) rate (° C./s) section (° C.) time (s) 26 L 550 700 1400 10 Two- 120 phase region 27 M 450 800 1000 10 Two- 120 phase region 28 N 400 750 1100 10 Two- 120 phase region 29 O 500 800 1500 10 Two- 120 phase region 30 P 550 700 1300 10 Two- 120 phase region 31 Q 450 800 1200 10 Two- 120 phase region 32 R 500 700 1400 10 Two- 120 phase region 33 S 550 750 1200 10 Two- 120 phase region 34 T 550 750 1100 10 Two- 120 phase region 35 U 400 800 1000 10 Two- 120 phase region 36 V 500 700 1200 10 Two- 120 phase region 37 W 450 800 1400 10 Two- 120 phase region 38 X 450 700 1500 10 Two- 120 phase region 39 Y 500 750 1100 10 Two- 120 phase region 40 XA 500 800 1300 10 Two- 120 phase region 41 XB 550 700 1400 10 Two- 120 phase region 42 XC 550 750 1000 10 Two- 120 phase region 43 XD 500 700 1200 10 Two- 120 phase region 44 XE 450 800 1400 10 Two- 120 phase region 45 XF 400 750 1200 10 Two- 120 phase region 46 XG 550 700 1100 10 Two- 120 phase region 47 XH 500 800 1300 10 Two- 120 phase region 48 XI 550 800 1500 10 Two- 120 phase region

TABLE 4 Primary Primary Secondary Secondary average cooling average Secondary average cooling stop heating maintaining Secondary cooling Specimen Steel rate temperature rate temperature maintaining rate No. type (° C./s) (° C.) (° C./s) (° C.) time (s) (° C./s) 1 A 20 220 15 450 300 10 2 A Poor pickling 3 A Occurrence of fracture during cold rolling 4 B Poor pickling 5 B Occurrence of fracture during cold rolling 6 B 20 210 15 400 300 10 7 B 0.5 180 15 450 300 10 8 B 20 190 15 400 300 10 9 B 20 120 15 400 300 10 10 B 20 210 15 400 300 10 11 C 20 200 15 450 600 10 12 C 20  80 15 400 300 10 13 C 20 330 15 400 300 10 14 C 20 220 15 270 300 10 15 C 20 230 15 530 300 10 16 C 20 180 15 400 40 10 17 C 20 180 15 450 144,000 10 18 D 20 210 15 400 300 10 19 E 20 230 15 400 300 10 20 F 20 280 15 400 300 10 21 G 20 220 15 400 300 10 22 H 20 220 15 350 300 10 23 I 20 180 15 400 600 10 24 J 20 200 15 400 300 10 25 K 20 220 15 450 300 10

TABLE 5 Primary Primary Secondary Secondary average cooling average Secondary Secondary average cooling stop heating maintaining maintaining cooling Specimen Steel rate temperature rate temperature time rate No. type (° C./s) (° C.) (° C./s) (° C.) (s) (° C./s) 26 L 20 210 15 400 300 10 27 M 20 220 15 400 300 10 28 N 20 190 15 400 300 10 29 O 20 180 15 450 300 10 30 P 20 200 15 450 300 10 31 Q 20 220 15 400 300 10 32 R 20 210 15 400 600 10 33 S 20 230 15 400 300 10 34 T 20 200 15 400 300 10 35 U 20 230 15 400 600 10 36 V 20 210 15 350 300 10 37 W 20 190 15 400 300 10 38 X 20 220 15 400 300 10 39 Y 20 200 15 450 300 10 40 XA 20 180 15 400 300 10 41 XB 20 200 15 400 300 10 42 XC 20 230 15 400 300 10 43 XD 20 200 15 400 300 10 44 XE 20 210 15 450 300 10 45 XF 20 190 15 400 300 10 46 XG 20 200 15 400 600 10 47 XH 20 220 15 400 300 10 48 XI 20 180 15 450 300 10

TABLE 6 Tempered Fresh Retained Specimen Steel Ferrite Bainite martensite martensite austenite Perlite No. type (vol. %) (vol. %) (vol. %) (vol. %) (vol. %) (vol. %) 1 A 12 17 52 0 19 0 2 A Poor pickling 3 A Occurrence of fracture during cold rolling 4 B Poor pickling 5 B Occurrence of fracture during cold rolling 6 B 1 23 61 0 15 0 7 B 24 14 46 0 5 11  8 B 5 17 62 0 16 0 9 B 10 18 54 0 18 0 10 B 12 15 53 1 19 0 11 C 11 21 51 0 17 0 12 C 9  5 79 0 7 0 13 C 12 63  6 0 19 0 14 C 10 14 72 0 4 0 15 C 8 18 67 1 6 0 16 C 9 12 73 0 6 0 17 C 11 19 59 4 7 0 18 D 11 18 51 1 19 0 19 E 10 17 57 0 16 0 20 F 5 21 54 0 20 0 21 G 6 41 39 0 14 0 22 H 18 15 51 0 16 0 23 I 11 16 56 0 17 0 24 J 9 12 61 0 18 0 25 K 7 13 46 0 34 0

TABLE 7 Tempered Fresh Retained Specimen Steel Ferrite Bainite martensite martensite austenite Perlite No. type (vol. %) (vol. %) (vol. %) (vol. %) (vol. %) (vol. %) 26 L 11 21 52 1 15 0 27 M 8 16 58 1 17 0 28 N 6 15 60 1 18 0 29 O 7 19 57 1 16 0 30 P 10 21 52 0 17 0 31 Q 8 17 59 1 15 0 32 R 7 16 42 0 35 0 33 S 11 18 49 1 21 0 34 T 10 19 53 0 18 0 35 U 9 20 54 1 16 0 36 V 8 17 55 0 20 0 37 W 11 18 54 0 17 0 38 X 10 22 47 0 21 0 39 Y 8 19 55 0 18 0 40 XA 10 17 59 0 14 0 41 XB 5 14 21 16 44 0 42 XC 11 22 62 0 5 0 43 XD 6 13 43 22 16 0 44 XE 5 17 40 19 19 0 45 XF 6 16 64 0 6 8 46 XG 4 15 51 15 15 0 47 XH 7 16 41 23 13 0 48 XI 6 20 44 18 12 0

TABLE 8 Specimen Steel [Si + Al]_(F)/ B_(T·E) B_(T·H) No. type [Si + Al]_(av) (MPa %) (MPa² %^(1/2)) R/t 1 A 1.17 31,542 10,819,415 1.58 2 A Poor pickling 3 A Occurrence of fracture during cold rolling 4 B Poor pickling 5 B Occurrence of fracture during cold rolling 6 B 0.97 28,215 6,485,296 2.03 7 B 1.53 16,328 7,229,178 2.16 8 B 1.26 29,631 8,992,265 1.62 9 B 1.14 30,027 12,855,180 2.25 10 B 1.22 32,592 10,502,114 1.88 11 C 1.20 30,894 9,899,273 2.14 12 C 1.48 16,442 7,778,447 4.15 13 C 1.18 20,611 6,655,107 2.37 14 C 1.54 13,607 7,272,268 4.38 15 C 1.49 20,851 8,568,314 2.03 16 C 1.57 16,874 8,352,875 5.19 17 C 1.52 19,866 7,780,616 2.40 18 D 1.29 30,894 9,635,245 1.52 19 E 1.37 32,250 10,772,531 2.72 20 F 1.43 29,236 10,505,903 1.94 21 G 1.15 31,333 11,214,821 1.27 22 H 1.10 30,017 9,804,695 2.75 23 I 1.28 29,537 10,028,681 2.52 24 J 1.21 31,044 9,925,290 1.78 25 K 1.11 30,314 10,070,923 1.97

TABLE 9 Specimen Steel [Si + Al]_(F)/ B_(T·E) B_(T·H) No. type [Si + Al]_(av) (MPa %) (MPa² %^(1/2)) R/t 26 L 1.23 30,502 10,152,414 1.72 27 M 1.27 28,899 11,180,290 1.85 28 N 1.20 32,692 9,987,755 1.79 29 O 1.16 35,909 10,225,208 2.23 30 P 1.12 29,106 10,502,607 1.43 31 Q 1.18 30,735 9,820,075 2.26 32 R 1.20 32,486 10,988,836 1.47 33 S 1.19 29,596 11,032,009 1.60 34 T 1.15 31,181 9,951,238 1.51 35 U 1.13 30,592 8,816,156 2.25 36 V 1.24 29,172 10,333,893 1.63 37 W 1.27 30,050 9,659,478 1.76 38 X 1.29 31,290 10,756,274 2.08 39 Y 1.14 30,294 11,088,165 2.04 40 XA 1.18 17,128 5,397,276 2.11 41 XB 1.22 20,732 5,914,019 5.53 42 XC 1.53 13,082 7,778,447 4.62 43 XD 1.15 24,944 8,709,941 4.81 44 XE 1.17 28,030 8,590,607 6.57 45 XF 1.49 15,485 7,857,409 2.26 46 XG 1.20 24,866 8,028,337 5.04 47 XH 1.27 23,463 7,721,541 5.38 48 XI 1.16 27,487 7,502,405 6.13

As shown in Tables 1 to 9 above, it could be seen that the specimens satisfying the conditions presented in the present invention simultaneously provide superior strength and workability since the value of [[Si+Al]_(F)/[Si+Al]_(av) satisfies the range of 0.4 to 1.45, the balance (TSXE1) of tensile strength and elongation is 22,000 MPa % or more, the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio is 7*10⁶ (MPa²%^(1/2)) or more, and the bendability (R/t) satisfies the range of 0.5 to 3.0.

It could be seen that, in specimens 2 to 5, since the alloy composition range of the present invention overlaps, but the hot-rolled annealing temperature and time are outside the range of the present invention, the pickling failure occurs or the fracture occurs during the cold rolling.

In specimen 6, the amount of ferrite formed was insufficient because the primary heating or maintaining temperature in the annealing heat treatment process after the cold rolling exceeded the range limited by the present invention. As a result, it could be seen that, in specimen 6, [Si+Al]_(F)/[Si+Al]_(av) was less than 1.02, and the balance of tensile strength and hole expansion ratio (TS²XHER^(1/2)) was less than 7*10⁶ (MPa²%^(1/2)).

In specimen 7, the primary cooling rate in the annealing heat treatment after the cold rolling did no reach the range limited by the present invention, so the ferrite was excessively formed and the retained austenite was formed less. As a result, it could be seen that, in specimen 7, [Si+Al]_(F)/[Si+Al]_(av) exceeds 1.45, and the balance (TSXE1) of tensile strength and elongation is less than 22,000 MPa %.

In specimen 12, the primary cooling stop temperature was low, so the tempered martensite was excessively formed and the retained austenite was formed less. As a result, it could be seen that, in specimen 12, [Si+Al]_(F)/[Si+Al]_(av) exceeds 1.45, the balance (TSXE1) of tensile strength and elongation is less than 22,000 MPa %, and the bendability (R/t) exceeds 3.0.

In Specimen 13, the primary cooling stop temperature was high, so the bainite was excessively formed and the tempered martensite was formed less. As a result, it could be seen that, in specimen 13, the balance (TSXE1) of tensile strength and elongation is less than 22,000 MPa % and the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio is less than 7*10⁶ (MPa²%^(1/2)).

In specimen 14, the secondary heating or maintaining temperature was low, so the tempered martensite was excessively formed and the retained austenite was formed less. As a result, it could be seen that, in specimen 14, [Si+Al]_(F)/[Si+Al]_(av) exceeds 1.45, the balance (TSXE1) of tensile strength and elongation is less than 22,000 MPa %, and the bendability (R/t) exceeds 3.0.

It could be seen that, in specimen 15, the secondary heating or maintaining temperature is high, so the amount of retained austenite formed is insufficient, [Si+Al]_(F)/[Si+Al]_(av) exceeds 1.45, and the balance (TSXE1) of tensile strength and elongation is less than 22,000 MPa %.

In specimen 16, the secondary maintaining time was insufficient, so the tempered martensite was excessively formed and the retained austenite was formed less. As a result, it could be seen that, in specimen 16, [Si+Al]_(F)/[Si+Al]_(av) exceeds 1.45, the balance (TSXE1) of tensile strength and elongation is less than 22,000 MPa %, and the bendability (R/t) exceeds 3.0.

It could be seen that, in specimen 17, the secondary maintaining time is excessive, so the amount of retained austenite formed is insufficient, [Si+Al]_(F)/[Si+Al]_(av) exceeds 1.45, and the balance (TSXE1) of tensile strength and elongation is less than 22,000 MPa %.

Specimens 40 to 48 may satisfy the manufacturing conditions presented in the present invention, but may be outside the alloy composition range. In these cases, it could be seen that [Si+Al]_(F)/[Si+Al]_(av), the balance (TSXE1) of tensile strength and elongation, and the balance (TS²XHER^(1/2)) of tensile strength and hole expansion ratio of the present invention does not simultaneously satisfy the conditions of 7*10⁶ (MPa²%^(1/2)) and the bendability (R/t). Meanwhile, it could be seen that, in specimen 42, when the total content of aluminum (Al) and silicon (Si) is less than 1.0%, the conditions of [Si+Al]_(F)/[Si+Al]_(av), the balance (TSXE1) of tensile strength and elongation, and the bendability (R/t) are not satisfied.

While the present invention has been described in detail through exemplary embodiment, other types of exemplary embodiments are also possible. Therefore, the technical spirit and scope of the claims set forth below are not limited to exemplary embodiments. 

1. A high strength steel sheet having superior workability, comprising: by wt %, C: 0.25 to 0.75%, Si: 4.0% or less, Mn: 0.9 to 5.0%, Al: 5.0% or less, P: 0.15% or less, S: 0.03% or less, N: 0.03% or less, a balance of Fe, and unavoidable impurities; and as microstructures, 30 to 70 vol % of tempered martensite, 10 to 45 vol % of bainite, 10 to 40 vol % of retained austenite, 3 to 20 vol % of ferrite, and an unavoidable structures, wherein the high-strength steel sheet satisfies the following [Relational Expression 1] 1.02≤[Si+Al]_(F)/[Si+Al]_(av)≤1.45  [Relational Expression 1] where [Si+Al]_(F) is an average total content (wt %) of Si and Al included in the ferrite, and [Si+Al]_(av) is an average total content (wt %) of Si and Al included in the retained austenite.
 2. The high strength steel sheet of claim 1, further comprising: one or more of the following (1) to (9): (1) one or more of Ti: 0 to 0.5%, Nb: 0 to 0.5%, and V: 0 to 0.5%; (2) one or more of Cr: 0 to 3.0% and Mo: 0 to 3.0%; (3) one or more of Cu: 0 to 4.5% and Ni: 0 to 4.5%; (4) B: 0 to 0.005%; (5) one or more of Ca: 0 to 0.05%, REM: 0 to 0.05% excluding Y, and Mg: 0 to 0.05%; (6) one or more of W: 0 to 0.5% and Zr: 0 to 0.5%; (7) one or more of Sb: 0 to 0.5% and Sn: 0 to 0.5%; (8) one or more of Y: 0 to 0.2% and Hf: 0 to 0.2%; and (9) Co: 0 to 1.5%.
 3. The high strength steel sheet of claim 1, wherein a total content (Si+Al) of Si and Al is 1.0 to 6.0 wt %.
 4. The high strength steel sheet of claim 1, wherein a balance B_(T·E) of tensile strength and elongation expressed by the following [Relational Expression 2] is 22,000 (MPa %) or more, a balance B_(T·H) of tensile strength and hole expansion ratio expressed by the following [Relational Expression 3] is 7*10⁶ (MPa²%^(1/2)) or more, and bendability B_(R) expressed by the following [Relational Expression 4] is 0.5 to 3.0, B _(T·E)=[Tensile Strength(TS, MPa)]²*[Elongation(El, %)]   [Relational Expression 2] B _(T·H)=[Tensile Strength(TS, MPa)]²*[Hole Expansion Ratio(HER, %)]^(1/2)  [Relational Expression 3] B _(R) =R/t  [Relational Expression 4] where R is a minimum bending radius (mm) at which cracks do not occur after a 90° bending test, and t is a thickness (mm) of the steel sheet.
 5. A method for manufacturing a high strength steel sheet having superior workability, the method comprising: heating and hot rolling a steel slab including, by wt %, C: 0.25 to 0.75%, Si: 4.0% or less, Mn: 0.9 to 5.0%, Al: 5.0% or less, P: 0.15% or less, S: 0.03% or less, N: 0.03% or less, a balance of Fe, and unavoidable impurities; coiling the hot-rolled steel sheet; performing hot-rolled annealing heat treatment on the coiled steel sheet in a temperature within a range of 650 to 850° C. for 600 to 1700 seconds; cold rolling the hot-rolled annealing heat-treated steel sheet; heating (primarily heating) the cold-rolled steel sheet to a temperature within a range of Ac1 or higher and less than Ac3 at an average temperature increase rate of 5° C./s or more, and maintaining (primarily maintaining) the primarily heated steel sheet for 50 seconds or more; cooling (primarily cooling) the primarily heated steel sheet to a temperature within a range of 100 to 300° C. at an average cooling rate of 1° C./s or more; heating (secondarily heating) the primarily cooled steel sheet to a temperature within a range of 300 to 500° C., and maintaining (secondarily maintaining) the primarily cooled steel sheet for 50 seconds or more; and cooling (secondarily cooling) the primarily cooled steel sheet to room temperature.
 6. The method of claim 5, wherein the steel slab further includes one or more of the following (1) to (9): (1) one or more of Ti: 0 to 0.5%, Nb: 0 to 0.5%, and V: 0 to 0.5%; (2) one or more of Cr: 0 to 3.0% and Mo: 0 to 3.0%; (3) one or more of Cu: 0 to 4.5% and Ni: 0 to 4.5%; (4) B: 0 to 0.005%; (5) one or more of Ca: 0 to 0.05%, REM: 0 to 0.05% excluding Y, and Mg: 0 to 0.05%; (6) one or more of W: 0 to 0.5% and Zr: 0 to 0.5%; (7) one or more of Sb: 0 to 0.5% and Sn: 0 to 0.5%; (8) one or more of Y: 0 to 0.2% and Hf: 0 to 0.2%; and (9) Co: 0 to 1.5%.
 7. The method of claim 5, wherein a total content (Si+Al) of Si and Al included in the steel slab is 1.0 to 6.0 wt %.
 8. The method of claim 5, wherein the steel slab is heated to a temperature within a range of 1000 to 1350° C., and is subjected to finish hot rolling in a temperature within a range of 800 to 1000° C.
 9. The method of claim 5, wherein the hot-rolled steel sheet is coiled in a temperature within a range of 300 to 600° C.
 10. The method of claim 5, wherein a reduction ratio of the cold rolling is 30 to 90%.
 11. The method of claim 5, wherein a cooling rate of the secondary cooling is 1° C./s or more. 